US5509978A - High strength and anti-corrosive aluminum-based alloy - Google Patents
High strength and anti-corrosive aluminum-based alloy Download PDFInfo
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- US5509978A US5509978A US08/385,915 US38591595A US5509978A US 5509978 A US5509978 A US 5509978A US 38591595 A US38591595 A US 38591595A US 5509978 A US5509978 A US 5509978A
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- the present invention relates to an aluminum-based alloy for use in a wide range of applications such as in aircraft, vehicles and ships, as well as, in the structural material for the engine portions thereof.
- the present invention may be employed as sash, roofing material and exterior material for use in construction, or as material for use in sea water equipment, nuclear reactors, and the like.
- alloys incorporating various components such as Al--Cu, Al--Si, Al--Mg, Al--Cu--Si, Al--Cu--Mg, and Al--Zn--Mg are known.
- superior anti-corrosive properties are obtained at a light weight, and thus the aforementioned alloys are being widely used as structural material for machines in vehicles, ships and aircraft, in addition to being employed as sash, roofing material, exterior material for use in construction, structural material for use in LNG tanks, and the like.
- the prior art aluminum-based alloys generally exhibit disadvantages such as a low hardness and poor heat resistance when compared to material incorporating Fe.
- some materials have incorporated elements such as Cu, Mg and Zn for increased hardness, disadvantages remain such as low anti-corrosive properties.
- an aluminum-based alloy which can be utilized as material with a high hardness, high strength, high electrical resistance, anti-abrasion properties, or as soldering material.
- the disclosed aluminum-based alloy has a superior heat resistance, and may undergo extruding or press processing by utilizing the superplastic phenomenon observed near liquid crystallization temperatures.
- This aluminum-based alloy comprises a composition AlM*X with a special composition ratio (wherein M* signifies an element such as V, Cr, Mn, Fe, Co, Ni, Cu, Zr and the like, and X represents a rare earth element such as La, Ce, Sm and Nd, or an element such as Y, Nb, Ta, Mm (misch metal) and the like), and has an amorphous or a combined amorphous/fine crystalline structure.
- M* signifies an element such as V, Cr, Mn, Fe, Co, Ni, Cu, Zr and the like
- X represents a rare earth element such as La, Ce, Sm and Nd, or an element such as Y, Nb, Ta, Mm (misch metal) and the like
- this aluminum-based alloy is disadvantageous in that high costs result from the incorporation of large amounts of expensive rare earth elements and/or metal elements with a high activity such as Y.
- problems also arise such as increased consumption and labor costs due to the large scale of the manufacturing facilities required to treat materials with high activities.
- the aforementioned aluminum-based alloy tends to display insufficient resistance to oxidation and corrosion.
- the first aspect of the present invention provides an aluminum-based alloy, essentially consisting of an amorphous structure or a multiphase amorphous/fine crystalline structure, represented by the general formula Al x M y R z (wherein M is at least one metal element selected from the group consisting of Ti, V, Cr, Mn, Fe, Co, Cu, Zr, Nb, Mo and Ni, and R is at least one element or mixture selected from the group consisting of Y, Ce, La, Nd and Mm (misch metal)).
- M is at least one metal element selected from the group consisting of Ti, V, Cr, Mn, Fe, Co, Cu, Zr, Nb, Mo and Ni
- R is at least one element or mixture selected from the group consisting of Y, Ce, La, Nd and Mm (misch metal)
- the second aspect of the present invention provides an aluminum-based alloy, essentially consisting of an amorphous structure or a multiphase amorphous/fine crystalline structure, represented by the general formula Al x Ni y M' z (wherein M' is at least one metal element selected from the group consisting of Ti, V, Mn, Fe, Co, Cu and Zr).
- M' is at least one metal element selected from the group consisting of Ti, V, Mn, Fe, Co, Cu and Zr.
- the fine crystalline component of the multiphase structure described in the aforementioned first and second aspects comprises at least one phase selected from the group consisting of an aluminum phase, a stable or metastable intermetallic compound phase, and a metal solid solution comprising an aluminum matrix.
- the individual crystal diameter of this fine crystalline component is approximately 30 to 50 nm.
- the fourth aspect of the present invention provides an aluminum-based alloy represented by the general formula Al x Co y M" z (wherein M"is at least one metal element selected from the group consisting of Mn, Fe and Cu).
- M is at least one metal element selected from the group consisting of Mn, Fe and Cu.
- the fifth aspect of the present invention provides an aluminum-based alloy represented by the general formula Al a Fe b L c (wherein L is at least one metal element selected from the group consisting of Mn and Cu).
- the sixth aspect of the present invention substitutes Ti or Zr in place of element M"or L, in an amount corresponding to one-half or less of the atomic percentage of M" or L.
- the atomic percentages of Al, element M, and element R are restricted to 64.5-95%, 5-35% and 0-0.4%, respectively. This is due to the fact that when the composition of any of the aforementioned elements fall outside these specified ranges, it becomes difficult to form an amorphous component, as well as a supersaturated solid solution in which the amount of solute exceeds the critical solid solubility; this, in turn, results in the objective of the present invention, an aluminum-based alloy having an amorphous structure, an amorphous/fine crystalline complex structure or a fine crystalline structure, being unobtainable using an industrial quenching process incorporating a liquid quenching method and the like.
- Element M which represents one or more metal elements selected from the group consisting of Ti, V, Cr, Mn, Fe, Co, Cu, Zr, Nb, Mo and Ni, coexists with R and improves the amorphous forming properties, as well as, raising the crystallization temperature of the amorphous phase. Most importantly, this element markedly improves the hardness and strength of the amorphous phase.
- these elements also stabilize the fine crystalline phase, form stable or metastable intermetallic compounds with aluminum or other additional elements, disperse uniformly in the aluminum matrix ( ⁇ -phase), phenomenally increase the hardness and strength of the alloy, suppress coarsening of the fine crystal at high temperatures, and impart a resistance to heat.
- an atomic percentage for element M of less than 5% is undesirable, as this reduces the strength and hardness of the alloy.
- an atomic percentage exceeding 35% is also undesirable as this results in intermetallic compounds forming easily, which in turn lead to embrittlement of the alloy.
- Element R is one or more elements selected from the group consisting of Y, Ce, La, Nd and Mm (misch metal).
- a misch metal mainly comprises La and/or Ce, and may also include additional complexes incorporating other rare earth metals, excluding the aforementioned La and Ce, as well as unavoidable impurities (Si, Fe, Mg, etc.).
- element R enhances the amorphous forming properties, and also raises the crystallization temperature of the amorphous phase. In this manner, the anti-corrosive properties can be improved, and the amorphous phase can be stabilized up to a high temperature. In addition, under the fine crystalline alloy manufacturing conditions, element R coexists with element M, and stabilizes the fine crystalline phase.
- the atomic percentages of Al, Ni, and element M' are restricted to 50-95%, 0.5-35% and 0.5-20%, respectively. This is due to the fact that when the composition of any of the aforementioned elements fall outside these specified ranges, it becomes difficult to form an amorphous component, as well as a supersaturated solid solution in which the amount of solute exceeds the critical solid solubility; this, in turn, results in the objective of the present invention, an aluminum-based alloy having an amorphous structure, an amorphous/fine crystalline complex structure or a fine crystalline structure, being unobtainable using an industrial quenching process incorporating a liquid quenching method.
- An atomic percentage for Al of less than 50% is undesirable, as this results in significant embrittlement of the alloy.
- an atomic percentage for Al exceeding 95% is also undesirable, as this results in reduction of the strength and hardness of the alloy.
- the atomic percentage for Ni is within the range of 0.5-35%. If the incorporated amount of Ni is less than 0.5%, the strength and hardness of the alloy are reduced. On the other hand, an atomic percentage exceeding 35% results in intermetallic compounds forming easily, which in turn leads to embrittlement of the alloy. Thus both of these situations are undesirable.
- the atomic percentage for element M' lies within the range of 0.5-20%. As in the aforementioned, if the incorporated amount of M' is less than 0.5%, the strength and hardness of the alloy are reduced. While, on the other hand, an atomic percentage exceeding 20% results in embrittlement of the alloy. Both of these situations are likewise undesirable.
- Element M' coexists with other elements, and improves the amorphous forming properties, in addition to raising the crystallization temperature of the amorphous phase. Most importantly, this element phenomenally improves the hardness and strength of the amorphous phase. As well, under the fine crystal manufacturing conditions, element M' also stabilizes the fine crystalline phase, forms stable or metastable intermetallic compounds with aluminum or other additional elements, disperses uniformly in the aluminum matrix ( ⁇ -phase), phenomenally increases the hardness and strength of the alloy, suppresses coarsening of the fine crystal at high temperatures, and imparts a resistance to heat.
- the aforementioned aluminium-based alloys according to the present invention represented by the formulae Al x Co y M"z and Al a Fe b L c , by adding predetermined amounts of Co and/or Fe to Al, the effect of quenching is enhanced, the amorphous and fine crystalline phases are more easily obtained, and the thermal stability of the overall structure is improved. In addition, the strength and hardness of the resulting alloy are also increased.
- the effect of quenching is enhanced, the amorphous and fine crystalline phases are more easily obtained, and the thermal stability of the overall structure is improved.
- the atomic percentage of Al is in the 50-95% range.
- An atomic percentage for Al of less than 50% is undesirable, as this results in embrittlement of the alloy.
- an atomic percentage for Al exceeding 95% is also undesirable, as this results in reduction of the strength and hardness of the alloy.
- the atomic percentage of Co and/or Fe lies in the 0.5-35% range.
- the strength and hardness are not improved, while, on the other hand, when this atomic percentage exceeds 35%, embrittlement is observed, and the strength and toughness are reduced.
- embrittlement of the alloy begins to occur.
- the atomic percentage of Mn (manganese) and/or Cu (copper) lies in the 0.5-20% range.
- Mn manganese
- Cu copper
- the atomic percentage of Ti (titanium) and/or Zr (zirconium) lies in the range of up to one-half the atomic percentage of element M" or L.
- the quench effect is not improved, and, in the case when a crystalline state is incorporated into the alloy composition, the crystalline grains are not finely crystallized.
- this atomic percentage exceeds 10%, embrittlement occurs, and toughness is reduced.
- the melting point rises, and melting become difficult to achieve.
- the viscosity of the liquid-melt increases, and thus, at the time of manufacturing, it becomes difficult to discharge this liquid-melt from the nozzle.
- All of the aforementioned aluminum-based alloys according to the present invention can be manufactured by quench solidification of the alloy liquid-melts having the aforementioned compositions using a liquid quenching method.
- This liquid quenching method essentially entails rapid cooling of the melted alloy.
- Single roll, double roll, and submerged rotational spin methods have proved to be particularly effective.
- a cooling rate of 10 4 to 10 6 K/sec is easily obtainable.
- the liquid-melt is first poured into a storage vessel such as a silica tube, and then discharged, via a nozzle aperture at the tip of the silica tube, towards a copper roll of diameter 30 to 300 mm, which is rotating at a fixed velocity in the range of 300 to 1000 rpm.
- a storage vessel such as a silica tube
- a nozzle aperture at the tip of the silica tube towards a copper roll of diameter 30 to 300 mm, which is rotating at a fixed velocity in the range of 300 to 1000 rpm.
- fine wire-thin material can be easily obtained through the submerged rotational spin method by discharging the liquid-melt in order to quench it, via the nozzle aperture, into a refrigerant solution layer of depth 1 to 10 cm, maintained by means of centrifugal force inside an air drum rotating at 50 to 500 rpm, under argon gas back pressure.
- the angle between the liquid-melt discharged from the nozzle, and the refrigerant surface is preferably 60° C. to 90° C.
- the relative velocity ratio of the the liquid-melt and the refrigerant surface is preferably 0.7 to 0.9.
- thin layers of aluminum-based alloy of the aforementioned compositions can also be obtained without using the above methods, by employing layer formation processes such as the sputtering method.
- aluminum alloy powder of the aforementioned compositions can be obtained by quenching the liquid-melt using various atomizer and spray methods such as a high pressure gas spray method. In the following, examples of structural states of the aluminum alloy obtained using the aforementioned methods are listed.
- Multiphase structure comprising an amorphous/Al fine crystalline phase
- Multiphase structure comprising an amorphous/stable or metastable intermetallic compound phase
- Multiphase structure comprising an Al/stable or metastable intermetallic compound or amorphous phase
- the fine crystalline phase of the present invention represents a crystalline phase in which the crystal particles have an average maximum diameter of 1 ⁇ m.
- the properties of the alloys possessing the aforementioned structural states are described in the following.
- An alloy of the structural state (amorphous phase) described in (1) above has a high strength, superior bending ductility, and a high toughness.
- Alloys possessing the structural phases (multiphase structures) described in (2) and (3) above have a high strength which is greater than that of the alloys of (amorphous) structural state (1) by a factor of 1.2 to 1.5.
- Alloys possessing the structural phases (multiphase structure and solid solution) described in (4) and (5) above have a greater toughness and higher strength than that of the alloys of structural states (1), (2) and (3).
- Each of the aforementioned structural states can be determined by a normal X-ray diffraction method or by observation using a transmission electron microscope.
- a halo pattern characteristic of this amorphous phase is evident.
- a diffraction pattern formed from a halo pattern and characteristic diffraction peak, attributed to the fine crystalline phase is displayed.
- a pattern formed from a halo pattern and characteristic diffraction peak, attributed to the intermetallic compound phase is displayed.
- amorphous and fine crystalline substances as well as, amorphous/fine crystalline complexes can be obtained by means of various methods such as the aforementioned single and double roll methods, submerged rotational spin method, sputtering method, various atomizer methods, spray method, mechanical alloying method and the like.
- the amorphous/fine crystalline multiphase can be obtained by selecting the appropriate manufacturing conditions as necessary.
- any of the structural states described in (1) to (3) above can be obtained.
- any of the structural states described in (4) and (5) can be obtained.
- the aforementioned amorphous phase structure is heated above a specific temperature, it decomposes to form crystal.
- This specific temperature is referred to as the crystallization temperature.
- the aluminum-based alloy of the present invention displays superplasticity at temperatures near the crystallization temperature (crystallization temperature ⁇ 100° C.), as well as, at the high temperatures within the fine crystalline stable temperature range, and thus processes such as extruding, pressing and hot forging can easily be performed. Consequently, aluminum-based alloys of the above-mentioned compositions obtained in the aforementioned thin tape, wire, plate and/or powder states can be easily formed into bulk materials by means of extruding, pressing and hot forging processes at the aforementioned temperatures. Furthermore, the aluminum-based alloys of the aforementioned compositions possess a high ductility, thus bending of 180° is also possible.
- the aluminum-based alloys having an amorphous phase or an amorphous/fine crystalline multiphase structure according to the present invention do not display structural or chemical non-uniformity of crystal grain boundary, segregation and the like, as seen in crystalline alloys. These alloys cause passivation due to formation of an aluminum oxide layer, and thus display a high resistance to corrosion.
- the tape alloy manufactured by means of the aforementioned quench process is pulverized in a ball mill, and then powder pressed in a vacuum hot press under vacuum (e.g. 10 -3 Torr) at a temperature slightly below the crystallization temperature (e.g. approximately 470K), thereby forming a billet for use in extruding with a diameter and length of several centimeters.
- This billet is set inside a container of an extruder, and is maintained at a temperature slightly greater than the crystallization temperature for several tens of minutes. Extruded materials can then be obtained in desired shapes such as round bars, etc. by extruding.
- the aluminum-based alloy according to the present invention is useful as materials with a high strength, hardness and resistance to corrosion. Furthermore, it is possible to improve the mechanical properties by heat treatment; this alloy also stands up well to bending, and thus possesses superior properties such as the ability to be mechanically processed.
- the aluminum-based alloys according to the present invention can be used in a wide range of applications such as in aircraft, vehicles and ships, as well as, in the structural material for the engine portions thereof.
- the aluminum-based alloys of the present invention may also be employed as sash, roofing material and exterior material for use in construction, or as material for use in sea water equipment, nuclear reactors, and the like.
- FIG. 1 shows a construction of an example of a single roll apparatus used at the time of manufacturing a tape of an alloy of the present invention following quench solidification.
- FIG. 2 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al 88 Ni 11 .6 Ce 0 .4.
- FIG. 3 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al 89 .7 Ni 5 Fe 5 Ce 0 .3.
- FIG. 4 shows the thermal properties of an alloy having the composition of Al 89 .6 Ni 5 Co 5 Ce 0 .4.
- FIG. 5 shows the thermal properties of an alloy having the composition of Al 88 Ni 11 .6 Y 0 .4.
- FIG. 6 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al x M 99 .7-x Y 0 .3 corresponding to various values of x.
- FIG. 7 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al x M 99 .7-x Ce 0 .3 corresponding to various values of x.
- FIG. 8 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al x M 99 .7-x La 0 .3 corresponding to various values of x.
- FIG. 9 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al 99 .6-y M y Ce 0 .4 corresponding to various values of y.
- FIG. 10 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al 99 .6-y M y Nd 0 .4 corresponding to various values of y.
- FIG. 11 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al 99 .6-y M y Mm 0 .4 corresponding to various values of y.
- FIG. 12 is a graph showing variation of the corrosion rate of alloys having the compositions of Al 89-z M 11 Y z corresponding to various values of z.
- FIG. 13 is a graph showing variation of the corrosion rate of alloys having the compositions of Al 89-z M 11 Nd z corresponding to various values of z.
- FIG. 14 is a graph showing variation of the corrosion rate of alloys having the compositions of Al 89-z M 11 La z corresponding to various values of z.
- FIG. 15 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al 87 Ni 12 Mn 1 .
- FIG. 16 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al 88 Ni 9 Co 3 .
- FIG. 17 shows the thermal properties of an alloy having the composition of Al 88 Ni 11 Zr 1 .
- FIG. 18 shows the thermal properties of an alloy having the composition of Al 88 Ni 11 Fe 1 .
- FIG. 19 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al x Ni 96-x M' 4 and Al x Ni 85-x M' 15 corresponding to various values of x.
- FIG. 20 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al x Ni 96-x M' 4 and Al x Ni 85-x M' 15 corresponding to various values of x.
- FIG. 21 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al 85-y Ni y M' 15 corresponding to various values of y.
- FIG. 22 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al 85-y Ni y M' 15 corresponding to various values of y.
- FIG. 23 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al 85-z Ni 15 M' z corresponding to various values of z.
- FIG. 24 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al 85-z Ni 15 M' z corresponding to various values of z.
- FIG. 25 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al 89 Co 8 Mn 3 .
- FIG. 26 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al 90 Co 6 Fe 4 .
- FIG. 27 shows the thermal properties of an alloy having the composition of Al 90 Co 9 Cu 1 .
- FIG. 28 shows the thermal properties of an alloy having the composition of Al 90 Co 9 Mn 1 .
- FIG. 29 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al x Co 96-x M" 4 and Al x Co 85-x M" 15 corresponding to various values of x.
- FIG. 30 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al 85-y Co y M" 15 corresponding to various values of y.
- FIG. 31 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al 85-z Co 15 M" z corresponding to various values of z.
- FIG. 32 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al a Fe 97-a L 3 and Al a Fe 85-a L 3 corresponding to various values of a.
- FIG. 33 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al 85-b Fe b L 15 corresponding to various values of b.
- FIG. 34 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al 85-c Fe 15 L c corresponding to various values of c.
- FIG. 35 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al 88 Co 6 M" 6 (1-a) Zr 6a corresponding to various values of a.
- FIG. 36 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al 88 Co 6 M" 6 (1-a) Ti 6a corresponding to various values of a.
- FIG. 37 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al 86 Fe 8 L 6 (1-x) Zr 6x corresponding to various values of x.
- FIG. 38 is a graph showing variation of the tensile rupture strength of alloys having the compositions of Al 86 Fe 8 L 6 (1-x) Ti 6x corresponding to various values of x.
- FIG. 39 is a graph showing structure-analysis data of an alloy having the composition of Al 70 Ge 20 Ni 10 , which was obtained in accordance with anomalous X-ray scattering.
- FIG. 40 is a graph showing structure-analysis data of an alloy having the composition of Al 70 Si 15 Ni 15 , which was obtained in accordance with anomalous X-ray scattering.
- FIG. 41 is a graph showing structure-analysis data of an alloy having the composition of Al 88 .7 Ni 11 Ce 0 .3, which was obtained in accordance with anomalous X-ray scattering.
- FIG. 42 is a graph showing structure-analysis data of an alloy having the composition of Al 88 Ni 11 Fe 1 , which was obtained in accordance with anomalous X-ray scattering.
- a molten alloy having a predetermined composition Al x M y R z was manufactured using a high frequency melting furnace. As shown in FIG. 1, this melt was poured into a silica tube 1 with a small aperture 5 (aperture diameter: 0.2 to 0.5 mm) at the tip, and then heat dissolved, following which the aforementioned silica tube 1 was positioned directly above copper roll 2. This roll 2 was then rotated at a high speed of 4000 rpm, and argon gas pressure (0.7 kg/cm 3 ) was applied to silica tube 1. Quench solidification was subsequently performed by discharging the liquid-melt 3 from small aperture 5 of silica tube 1 onto the surface of roll 2 and quenching to yield an alloy tape 4.
- the samples according to the present invention display an extremely high hardness from 260 to 340 DPN.
- FIG. 2 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al 88 Ni 11 .6 Ce 0 .4.
- the crystal peak appears as a broad peak pattern with the alloy sample displaying an amorphous single phase structure.
- FIG. 3 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al 89 .7 Ni 5 Fe 5 Ce 0 .3.
- a two-phase structure is displayed in which fine Al particles having an fcc structure of the nano-scale are dispersed into the amorphous phase.
- (111) and (200) display the crystal peaks of Al having an fcc structure.
- FIG. 4 shows the DSC (Differential Scanning Calorimetry) curve in the case when an alloy having the composition of Al 89 .6 Ni 5 Co 5 Ce 0 .4 is heated at an increase temperature rate of 0.67 K/s.
- FIG. 5 shows the DSC curve in the case when an alloy having the composition of Al 88 Ni 11 .6 Y 0 .4 is heated at an increase temperature rate of 0 .67 K/s.
- the broad peak appearing at lower temperatures represents the crystallization peak of Al particles having an fcc structure, while the sharp peak at higher temperatures represents the crystallization peak of the alloys. Due to the existence of these two peaks, when performing heat treatment such as quench hardening at an appropriate temperature, the volume percentage of the Al particles dispersed into the amorphous matrix phase can be controlled. As a result, it is clear that the mechanical properties can be improved through heat treatment.
- FIGS. 6-14 are provided.
- the graph in FIG. 6 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al x M 99 .7-x Y 0 .3 (in which element M is Ti, V, Cr, or Mn) corresponding to various values of x.
- the graph in FIG. 7 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al x M 99 .7-x Ce 0 .3 (in which element M is Fe, Ni, Co, or Cu) corresponding to various values of x.
- the graph in FIG. 8 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al x M 99 .7-x La 0 .3 (in which element M is Zr, Nb, or Mo) corresponding to various values of x.
- the graph in FIG. 9 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al 99 .6-y M y Ce 0 .4 (in which element M is Ti, V, Cr, or Mn) corresponding to various values of y.
- the graph in FIG. 10 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al 99 .6-y M y Nd 0 .4 (in which element M is Fe, Ni, Co, or Cu) corresponding to various values of y.
- the graph in FIG. 11 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al 99 .6-y M y Mm 0 .4 (in which element M is Zr, Nb, or Mo) corresponding to various values of y.
- the graph in FIG. 12 shows variation of the corrosion rate (in 1N-HCl solution) of alloys having the compositions of Al 89-z M 11 Y z (in which element M is Ti, V, Cr, or Mn) corresponding to various values of z.
- the graph in FIG. 13 shows variation of the corrosion rate (in 1N-HCl solution) of alloys having the compositions of Al 89-z M 11 Nd z (in which element M is Fe, Ni, Co, or Cu) corresponding to various values of z.
- the graph in FIG. 14 shows variation of the corrosion rate (in 1N-HCl solution) of alloys having the compositions of Al 89-z M 11 La z (in which element M is Zr, Nb, or corresponding to various values of z.
- a molten alloy having a predetermined composition Al x Ni y M' z was manufactured using a high frequency melting furnace. As shown in FIG. 1, this melt was poured into a silica tube 1 with a small aperture 5 (aperture diameter: 0.2 to 0.5 mm) at the tip, and then heat dissolved, following which the aforementioned silica tube 1 was positioned directly above copper roll 2. This roll 2 was then rotated at a high speed of 4000 rpm, and argon gas pressure (0.7kg/cm 3 ) was applied to silica tube 1. Quench solidification was subsequently performed by discharging the liquid-melt from small aperture 5 of silica tube 1 onto the surface of roll 2 and quenching to yield an alloy tape 4.
- the 180° contact bending test was conducted by bending each alloy tape sample 180° and contacting the ends thereby forming a U-shape.
- the samples according to the present invention shown in Tables 3 and 4 display an extremely high hardness ranging from 260 to 400 DPN.
- FIG. 15 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al 87 Ni 12 Mn 1 .
- the crystal peak appears as a broad peak pattern with the alloy sample displaying an amorphous single phase structure.
- FIG. 16 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al 88 Ni 9 Co 3 .
- a two-phase structure is displayed in which fine Al particles having an fcc structure of the nano-scale are dispersed into the amorphous phase.
- (111) and (200) display the crystal peaks of Al having an fcc structure.
- FIG. 17 shows the DSC (Differential Scanning Calorimetry) curve in the case when an alloy having the composition of Al88Ni 11 Zr 1 is heated at an increase temperature rate of 0.67 K/s.
- FIG. 18 shows the DSC curve in the case when an alloy having the composition of Al 88 Ni 11 Fe 1 is heated at an increase temperature rate of 0.67 K/s.
- the broad peak appearing at lower temperatures represents the crystallization peak of Al particles having an fcc structure, while the sharp peak at higher temperatures represents the crystallization peak of the alloys. Due to the existence of these two peaks, when performing heat treatment such as quench hardening at an appropriate temperature, the volume percentage of the Al particles dispersed into the amorphous matrix phase can be controlled. As a result, it is clear that the mechanical properties can be improved through heat treatment.
- FIGS. 19-24 are provided.
- the graph in FIG. 19 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al x Ni 96-x M' 4 and Al x Ni 85-x M' 15 (in which element M' is Ti, V, Cr, or Mn) corresponding to various values of x.
- the graph in FIG. 20 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al x Ni 96-x M' 4 and Al x Ni 85-x M' 15 (in which element M' is Co, Cu, or Zr) corresponding to various values of x.
- the graph in FIG. 21 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al 85-y Ni y M' 15 (in which element M' is Ti, V, Mn, or Fe) corresponding to various values of y.
- the graph in FIG. 22 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al 85-y Ni y M' 15 (in which element M' is Co, Cu, or Zr) corresponding to various values of y.
- the graph in FIG. 23 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al 85-z Ni 15 M' z (in which element M' is Ti, V, Mn, or Fe) corresponding to various values of z.
- the graph in FIG. 24 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al 85-z Ni 15 M' z (in which element M' is Co, Cu, or Zr) corresponding to various values of z.
- a molten alloy having a predetermined composition Al x Co y M" z or Al a Fe b L c was manufactured using a high frequency melting furnace. As shown in FIG. 1, this melt was poured into a silica tube 1 with a small aperture 5 (aperture diameter: 0.2 to 0.5 mm) at the tip, and then heat dissolved, following which the aforementioned silica tube 1 was positioned directly above copper roll 2. This roll 2 was then rotated at a high speed of 4000 rpm, and argon gas pressure (0.7kg/cm 3 ) was applied to silica tube 1. Quench solidification was subsequently performed by discharging the liquid-melt from small aperture 5 of silica tube 1 onto the surface of roll 2 and quenching to yield an alloy tape 4.
- the samples according to the present invention shown in Tables 5 and 7 display an extremely high hardness ranging from 165 to 387 DPN.
- FIG. 25 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al 89 Co 8 Mn 3 .
- the crystal peak appears as a broad peak pattern with the alloy sample displaying an amorphous single phase structure.
- FIG. 26 shows the analysis result of the X-ray diffraction of an alloy having the composition of Al 90 Co 6 Fe 4 .
- a multiphase structure is displayed which comprises an amorphous phase and a fine Al crystalline phase having an fcc structure of the nanoscale.
- (111) and (200) display the crystal peaks of Al having an fcc structure.
- FIG. 27 shows the DSC (Differential Scanning Calorimetry) curve in the case when an alloy having the composition of Al 90 Co 9 Cu 1 is heated at an increase temperature rate of 0.67 K/s.
- FIG. 28 shows the DSC curve in the case when an alloy having the composition of Al 90 Co 9 Mn 1 is heated at an increase temperature rate of 0.67 K/s.
- the broad peak appearing at lower temperatures represents the crystallization peak of Al particles having an fcc structure, while the sharp peak at higher temperatures represents the crystallization peak of the alloys. Due to the existence of these two peaks, when performing heat treatment such as quench hardening at an appropriate temperature, the volume percentage of the Al particles dispersed into the amorphous matrix phase can be controlled. As a result, it is clear that the mechanical properties can be improved through heat treatment.
- FIGS. 29-38 are provided.
- the graph in FIG. 29 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al x Co 96-x M" 4 and Al x Co 85-x M" 15 (in which element M" is Mn, Fe, or Cu) corresponding to various values of x. According to this graph, it can be seen that an alloy having a composition of Al x Co y M" z in which the atomic percentage for Al is less than 50% or exceeds 95% is undesirable, since such an alloy may not have sufficient strength.
- the graph in FIG. 30 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al 85-y Co y M" 15 (in which element M" is Mn, Fe, or Cu) corresponding to various values of y. According to this graph, it can be seen that an alloy having a composition of Al x Co y M" z in which the atomic percentage for Co is less than 0.5% or exceeds 35% is undesirable, since such an alloy may not have sufficient strength.
- the graph in FIG. 31 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al 85-z Co 15 M" z (in which element M" is Mn, Fe, or Cu) corresponding to various values of z. According to this graph, it can be seen that an alloy having a composition of Al x Co y M" z in which the atomic percentage for element M" is less than 0.5% or exceeds 20% is undesirable, since such an alloy may not have sufficient strength.
- the graph in FIG. 32 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al a Fe 97-a L 3 and Al a Fe 85-a L 3 (in which L is Mn or Cu) corresponding to various values of a. According to this graph, it can be seen that an alloy having a composition of Al a Fe b L c in which the atomic percentage for Al is less than 50% or exceeds 95% is undesirable, since such an alloy may not have sufficient strength.
- the graph in FIG. 33 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al 85-b Fe b L 15 (in which L is Mn or Cu) corresponding to various values of b. According to this graph, it can be seen that an alloy having a composition of Al a Fe b L c in which the atomic percentage for Fe is less than 0.5% or exceeds 35% is undesirable, since such an alloy may not have sufficient strength.
- the graph in FIG. 34 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al 85-c Fe 15 L c (in which L is Mn or Cu) corresponding to various values of c. According to this graph, it can be seen that an alloy having a composition of Al a Fe b L c in which the atomic percentage for L is less than 0.5% or exceeds 20% is undesirable, since such an alloy may not have sufficient strength.
- the graph in FIG. 35 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al 88 Co 6 M" 6 (1-a) Zr 6a (in which element M" is Mn, Fe, or Cu) corresponding to various values of a. According to this graph, it can be seen that an alloy having a composition of Al x Co y M" z in which a part of element M" is substituted by Zr but in which the atomic percentage for Zr exceeds onehalf of that of element M" is undesirable, since such an alloy may not have sufficient strength.
- the graph in FIG. 36 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al 88 Co 6 M" 6 (1-a) Ti 6a (in which element M" is Mn, Fe, or Cu) corresponding to various values of a. According to this graph, it can be seen that an alloy having a composition of Al x Co y M" z in which a part of element M" is substituted by Ti but in which the atomic percentage for Ti exceeds one-half of that of element M" is undesirable, since such an alloy may not have sufficient strength.
- the graph in FIG. 37 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al 86 Fe 8 L 6 (1-x) Zr 6x (in which L is Mn or Cu) corresponding to various values of x. According to this graph, it can be seen that an alloy having a composition of Al a Fe b L c in which a part of L is substituted by Zr but in which the atomic percentage for Zr exceeds one-half of that of L is undesirable, since such an alloy may not have sufficient strength.
- the graph in FIG. 38 shows variation of the tensile rupture strength ( ⁇ f) of alloys having the compositions of Al 86 Fe 8 L 6 (1-x) Ti 6x (in which L is Mn or Cu) corresponding to various values of x. According to this graph, it can be seen that an alloy having a composition of Al a Fe b L c in which a part of L is substituted by Ti but in which the atomic percentage for Ti exceeds one-half of that of L is undesirable, since such an alloy may not have sufficient strength.
- U.S. Pat. No. 4,595,429 discloses alloys having the composition Al a M b M' c X d Y e , in which: 50 ⁇ a ⁇ 95 atom %; M representing one or more metals of the group Mn, Ni, Cu, Zr, Ti, C, Cr, Fe, and Co, with 0 ⁇ b ⁇ 40 atom %; M' representing Mo and/or W, with 0 ⁇ c ⁇ 15 atom %; X representing one or more elements of the group Ca, Li, Mg, Ge, Si, and Zn, with 0 ⁇ d ⁇ 20 atom %; and Y representing impurities such as O, N, C, H, He, Ga, etc., the proportions of which does not exceed 3 atom %.
- the alloys according to Le Caer, et al. are similar in composition to the alloys according to the present invention, the alloys of Le Caer, et al., do not possess sufficient bending ductility or tensile strength.
- FIG. 41 is a graph showing structure-analysis data of an alloy according to the present invention having the composition of Al 88 .7 Ni 11 Ce 0 .3.
- FIG. 42 is a graph showing structure-analysis data of an alloy according to the present invention having the composition of Al 88 Ni 11 Fe 1 .
- one axis (Q) represents the wave number vector
- the other axis ( ⁇ I(Q)) represents the differential intensity profile at incident energy.
- the differential intensity profile values are partially negative, and this indicates the existence of a short periodical regular array of elements which produces a brittle amorphous structure. Accordingly, these alloys do not have bending ductility.
- the differential intensity profile is always positive for any value of the wave number vector. This indicates that the amorphous structures of the alloys according to the present invention are homogeneous, on the whole, and the alloys exhibit bending ductility. This makes a test of the tensile strength possible and it is found that the alloys of the present invention possess a high strength of over 750 MPa and a desirable Vickers hardness in the range of 150-385.
Abstract
Description
TABLE 1 __________________________________________________________________________ Sample Alloy composition Structural Bending No. (at %) σf (MPa) Hv (DPN) state test __________________________________________________________________________ 1 Al.sub.89.6 Ni.sub.5 Co.sub.5 Ce.sub.0.4 1240 317 fcc-Al + Amo Duc 2 Al.sub.88.7 Ni.sub.11 Nd.sub.0.3 1170 305 fcc-Al + Amo Duc 3 Al.sub.88.7 Ni.sub.11 La.sub.0.3 1050 260 amorphous Duc 4 Al.sub.88.7 Ni.sub.11 Ce.sub.0.3 1030 272 amorphous Duc 5 Al.sub.88.7 Cu.sub.11 Y.sub.0.3 1190 310 fcc-Al + Amo Duc 6 Al.sub.88.7 Mn.sub.11 Ce.sub.0.3 910 307 fcc-Al + Amo Duc 7 Al.sub.88.7 Fe.sub.11 Mn.sub.0.3 900 298 fcc-Al + Amo Duc 8 Al.sub.87.6 Ni.sub.11 Cr.sub.1 Y.sub.0.4 800 340 fcc-Al + Amo Duc 9 Al.sub.87.6 Ni.sub.11 V.sub.1 Y.sub.0.4 840 305 amorphous Duc 10 Al.sub.87.6 Ni.sub.11 Ti.sub.1 Y.sub.0.4 1030 332 amorphous Duc 11 Al.sub.87.6 Ni.sub.11 Zr.sub.1 Ce.sub.0.4 960 280 amorphous Duc 12 Al.sub.87.6 Ni.sub.11 Nb.sub.1 Ce.sub.0.4 980 317 fcc-Al + Amo Duc 13 Al.sub.87.6 Ni.sub.11 Mo.sub.1 Ce.sub.0.4 1020 320 fcc-Al + Amo Duc __________________________________________________________________________
TABLE 2 ______________________________________ Sam- ple Alloy composition σf Hv Structural Bending No. (at %) (MPa) (DPN) state test ______________________________________ 14 Al.sub.60.7 Fe.sub.39 Y.sub.0.3 --*.sup.1 520Crystalline Bri 15 Al.sub.98.7 Fe.sub.1 Ce.sub.0.3 440 120 fcc-Al Duc 16 Al.sub.99.7 Ce.sub.0.3 400 107 fcc-Al Duc 17 Al.sub.60 Fe.sub.40 --*.sup.1 520 Crystalline Bri ______________________________________ *.sup.1 Tensile test could not be conducted due to brittle nature.
TABLE 3 ______________________________________ Sam- Alloy ple composition σf Hv Structural Bending No. (at %) (MPa) (DPN) state test ______________________________________ 18 Al.sub.88 Ni.sub.7 Co.sub.5 1065 316 amorphous Duc 19 Al.sub.88 Ni.sub.8 Co.sub.4 1061 313 amorphous Duc 20 Al.sub.88 Ni.sub.9 Co.sub.3 996 307 amorphous Duc 21 Al.sub.88 Ni.sub.10 Co.sub.2 813 306 fcc-Al + Amo Duc 22 Al.sub.88 Ni.sub.11 Co.sub.1 931 295 fcc-Al + Amo Duc 23 Al.sub.88 Ni.sub.8 Fe.sub.4 1080 302 fcc-Al + Amo Duc 24 Al.sub.88 Ni.sub.9 Fe.sub.3 960 309 fcc-Al + Amo Duc 25 Al.sub.88 Ni.sub.10 Fe.sub.2 915 304 fcc-Al + Amo Duc 26 Al.sub.88 Ni.sub.11 Fe.sub.1 928 311 fcc-Al + Amo Duc 27 Al.sub.88 Ni.sub.11 Cu.sub.1 780 327 fcc-Al + Amo Duc 28 Al.sub.88 Ni.sub.11 Mn.sub.1 930 302 fcc-Al + Amo Duc 29 Al.sub.88 Ni.sub.11 V.sub.1 797 363 fcc-Al + Amo Duc 30 Al.sub.88 Ni.sub.11 Ti.sub.1 1047 368 fcc-Al + Amo Duc 31 Al.sub.88 Ni.sub.11 Zr.sub.1 954 276 fcc-Al + Amo Duc ______________________________________
TABLE 4 ______________________________________ Alloy Sample composition σf Hv Structural Bending No. (at %) (MPa) (DPN) state test ______________________________________ 32 Al.sub.90 Ni.sub.5 Co.sub.5 1150 380 fcc-Al + Duc Amo 33 Al.sub.87 Ni.sub.12 Mn.sub.1 953 262 amorphous Duc 34 Al.sub.88 Ni.sub.7 V.sub.5 1070 331 fcc-Al +Duc Amo 35 Al.sub.95 Ni.sub.0.3 Cu.sub.4.7 420 117 fcc-Al Duc 36 Al.sub.95 Ni.sub.0.3 Cu.sub.4.7 400 109 fcc-Al Duc 37 Al.sub.95 Ni.sub.0.3 Fe.sub.4.7 450 123 fcc-Al Duc 38 Al.sub.88 Mn.sub.12 --*.sup.1 550 Crystalline Bri 39 Al.sub.73 Ni.sub.2 Fe.sub.25 --*.sup.1 570Crystalline Bri 40 Al.sub.50 Ni.sub.40 Fe.sub.10 --*.sup.1 530 Crystalline Bri 41 Al.sub.94.6 Ni.sub.5 Cu.sub.0.4 380 102 fcc-Al Duc 42 Al.sub.94 Ni.sub.6 540 180 fcc-Al Duc 43 Al.sub.96 Ni.sub.2 Co.sub.2 400 120 fcc-Al Duc 44 Al.sub.55 Ni.sub.40 Fe.sub.5 --*.sup.1 520 Crystalline Bri ______________________________________ *.sup.1 Tensile test could not be conducted due to brittle nature.
TABLE 5 __________________________________________________________________________ Alloy composition (Subscript numerals Sample represent atomic σf Hv Structural Bending No. percentage) (MPa) (DPN) state test __________________________________________________________________________ 45 Al.sub.98 Co.sub.1 Mn.sub.1 400 110 fcc-Al Duc Comparative example 46 Al.sub.95 Co.sub.4 Mn.sub.1 780 215 fcc-Al Duc Example 47 Al.sub.90 Co.sub.8 Mn.sub.2 1270 330 fcc-Al + Amo Duc Example 48 Al.sub.80 Co.sub.15 Mn.sub.5 1115 315 fcc-Al + Amo Duc Example 49 Al.sub.70 Co.sub.25 Mn.sub.5 1210 320 fcc-Al + Amo Duc Example 50 Al.sub.60 Co.sub.30 Mn.sub.10 980 370 Amo + Com Duc Example 51 Al.sub.50 Co.sub.30 Mn.sub.20 960 360 Amo + Com Duc Example 52 Al.sub.45 Co.sub.35 Mn.sub.20 -- 550 Com Bri Comparative example 53 Al.sub.50 Co.sub.40 Mn.sub.10 -- 490 Com Bri Comparative example 54 Al.sub.60 Co.sub.35 Mn.sub.5 960 370 Amo + Com Duc Example 55 Al.sub.65 Co.sub.30 Mn.sub.5 975 340 fcc-Al + Amo Duc Example 56 Al.sub.70 Co.sub.20 Mn.sub.10 1010 340 fcc-Al + Amo Duc Example 57 Al.sub.80 Co.sub.10 Mn.sub.10 1015 345 fcc-Al + Amo Duc Example 58 Al.sub.96 Co.sub.1 Mn.sub.3 760 180 fcc-Al Duc Example 59 Al.sub.95 Co.sub.0.5 Mn.sub.4.5 760 165 fcc-Al Duc Example 60 Al.sub.94 Co.sub.0.3 Mn.sub.5.7 445 85 fcc-Al Duc Comparative example __________________________________________________________________________
TABLE 6 __________________________________________________________________________ Alloy composition (Subscript numerals Sample represent atomic σf Hv Structural Bending No. percentage) (MPa) (DPN) state test __________________________________________________________________________ 61 Al.sub.70 Co.sub.5 Mn.sub.25 -- 520 Com Bri Comparative example 62 Al.sub.72 Co.sub.8 Mn.sub.20 1195 360 Amo + Com Duc Example 63 Al.sub..sub.80 Co.sub.10 Mn.sub.10 1145 320 fcc-Al + Amo Duc Example 64 Al.sub.89 Co.sub.10 Mn.sub.1 1230 387 fcc-Al + Amo Duc Example 65 Al.sub.91 Co.sub.8.5 Mn.sub.0.5 1200 330 fcc-Al + Amo Duc Example 66 Al.sub.89 Co.sub.10.7 Mn.sub.0.3 460 120 fcc-Al + Amo Duc Comparative example 67 Al.sub.98 Co.sub.1 Fe.sub.1 420 125 fcc-Al Duc Comparative example 68 Al.sub.80 Co.sub.10 Fe.sub.10 1010 295 fcc-Al + Amo Duc Example 69 Al.sub.45 Co.sub.35 Fe.sub.20 -- 510 Com Bri Comparative example 70 Al.sub.89 Co.sub.10.7 Fe.sub.0.3 390 105 fcc-Al + Amo Duc Comparative example 71 Al.sub.98 Co.sub.1 Cu.sub.1 320 80 fcc-Al Duc Comparative example 72 Al.sub.70 Co.sub.25 Cu.sub.5 1005 325 fcc-Al + Amo Duc Example 73 Al.sub.45 Co.sub.35 Cu.sub.20 -- 505 Com Bri Comparative example 74 Al.sub..sub.89.7 Co.sub.10 Cu.sub.0.3 485 112 fcc-Al + Amo Duc Comparative example 75 Al.sub.90 Co.sub.9 Mn.sub.0.5 Fe.sub.0.5 996 305 fcc-Al + Amo Duc Example 76 Al.sub.89 Co.sub.8 Mn.sub.2 Cu.sub.1 1210 340 fcc-Al + Amo Duc Example 77 Al.sub.90 Co.sub.7 Fe.sub.1 Cu.sub.1 1005 298 fcc-Al + Amo Duc Example 78 Al.sub.90 Co.sub.7 Mn.sub.1 Fe.sub.1 Cu.sub.1 1230 310 fcc-Al + Amo Duc Example __________________________________________________________________________
TABLE 7 __________________________________________________________________________ Alloy composition (Subscript numerals Sample represent atomic σf Hv Structural Bending No. percentage) (MPa) (DPN) state test __________________________________________________________________________ 79 Al.sub.50 Fe.sub.40 Mn.sub.10 -- 560 Com Bri Comparative example 80 Al.sub.60 Fe.sub.35 Mn.sub.5 845 363 fcc-Al + Amo Duc Example 81 Al.sub.65 Fe.sub.30 Mn.sub.5 960 375 fcc-Al + Amo Duc Example 82 Al.sub.70 Fe.sub.20 Mn.sub.10 875 340 fcc-Al + Amo Duc Example 83 Al.sub.85 Fe.sub.10 Mn.sub.5 1070 360 fcc-Al + Amo Duc Example 84 Al.sub.95 Fe.sub.0.5 Mn.sub.4.5 910 260 fcc-Al + Amo Duc Example 85 Al.sub.94 Fe.sub.0.3 Mn.sub.5.7 480 113 fcc-Al Duc Comparative example 86 Al.sub.92 Fe.sub.6 Cu.sub.2 1005 276 fcc-Al + Amo Duc Example 87 Al.sub.88 Fe.sub.8 Cu.sub.4 1210 302 fcc-Al + Amo Duc Example 88 Al.sub.45 Fe.sub.35 Cu.sub.20 -- 560 Com Bri Comparative example 89 Al.sub.90 Fe.sub.6 Mn.sub.2 Cu.sub.2 1112 293 fcc-Al + Amo Duc Example 90 Al.sub.75 Co.sub.8 Mn.sub.5 Ti.sub.12 -- 511 fcc-Al + Com Bri Comparative example 91 Al.sub.76 Fe.sub.4 Mn.sub.10 Ti.sub.10 1210 370 fcc-Al + Amo Duc Example 92 Al.sub.78 Co.sub.4 Fe.sub.10 Zr.sub.8 1100 359 Amo Duc Example 93 Al.sub.78 Fe.sub.8 Cu.sub.8 Ti.sub.6 1060 360 fcc-Al + Amo Duc Example 94 Al.sub..sub.82 Co.sub.8 Mn.sub.3 Fe.sub.3 Zr.sub.4 1090 305 Amo Duc Example 95 Al.sub..sub.83 Fe.sub.6 Mn.sub.3 Cu.sub.6 Ti.sub.2 1206 328 fcc-Al + Amo Duc Example 96 Al.sub..sub.83 Co.sub.8 Mn.sub.4 Fe.sub.4 Zr.sub.1 1230 345 fcc-Al + Amo Duc Example 97 Al.sub.98 Fe.sub.7 Cu.sub.4.5 Ti.sub.0.5 1175 339 fcc-Al + Amo Duc Example 98 Al.sub.85 Fe.sub.10 Mn.sub.4.7 Zr.sub.0.3 1049 362 fcc-Al + Amo Duc Comparative example __________________________________________________________________________
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